WO2012017695A1 - Grain-oriented magnetic steel sheet - Google Patents
Grain-oriented magnetic steel sheet Download PDFInfo
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- WO2012017695A1 WO2012017695A1 PCT/JP2011/004479 JP2011004479W WO2012017695A1 WO 2012017695 A1 WO2012017695 A1 WO 2012017695A1 JP 2011004479 W JP2011004479 W JP 2011004479W WO 2012017695 A1 WO2012017695 A1 WO 2012017695A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1283—Application of a separating or insulating coating
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1288—Application of a tension-inducing coating
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
- H01F1/18—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets with insulating coating
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12389—All metal or with adjacent metals having variation in thickness
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12535—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.] with additional, spatially distinct nonmetal component
- Y10T428/12597—Noncrystalline silica or noncrystalline plural-oxide component [e.g., glass, etc.]
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12535—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.] with additional, spatially distinct nonmetal component
- Y10T428/12611—Oxide-containing component
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
- Y10T428/24479—Structurally defined web or sheet [e.g., overall dimension, etc.] including variation in thickness
- Y10T428/2457—Parallel ribs and/or grooves
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y10T428/24612—Composite web or sheet
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
- Y10T428/24942—Structurally defined web or sheet [e.g., overall dimension, etc.] including components having same physical characteristic in differing degree
Definitions
- the present invention relates to a grain-oriented electrical steel sheet used for a core material such as a transformer.
- the grain-oriented electrical steel sheet is mainly used as an iron core of a transformer and is required to have excellent magnetization characteristics, particularly low iron loss.
- it is important to highly align the secondary recrystallized grains in the steel sheet in the (110) [001] orientation (so-called Goth orientation) and to reduce impurities in the product steel sheet.
- control of crystal orientation and reduction of impurities are limited in view of the manufacturing cost.
- a technique for reducing the iron loss by introducing non-uniform strains or grooves into the surface of the steel sheet by physical or chemical techniques and subdividing the width of the magnetic domain that is, a magnetic domain refinement technique has been developed.
- Patent Document 1 proposes a technique for reducing the iron loss of a steel sheet by irradiating a final product plate with a laser, introducing a high dislocation density region into the steel sheet surface layer, and narrowing the magnetic domain width.
- Patent Document 2 a steel sheet that has been subjected to finish annealing is formed with a groove having a depth of more than 5 ⁇ m in the base iron portion under a load of 882 to 2156 MPa (90 to 220 kgf / mm 2 ), and then 750
- Patent Document 3 proposes a technique for introducing linear notches (grooves) having a width of 30 ⁇ m or more and 300 ⁇ m or less, a depth of 10 ⁇ m or more and 70 ⁇ m or less, and an interval of 1 mm or more in the rolling direction in a direction substantially perpendicular to the rolling direction of the steel sheet. Yes. With the development of the magnetic domain fragmentation technology as described above, grain oriented electrical steel sheets having good iron loss characteristics have been obtained.
- the directional electrical steel sheet is provided with a tension coating mainly composed of silica and phosphate.
- This tension coating has the effect of generating tensile stress in the grain-oriented electrical steel sheet, improving magnetostriction characteristics and reducing transformer noise.
- Patent Document 4 Patent Document 5 and Patent Document 6 contain colloidal silica and phosphate, and further, one or more selected from chromic anhydride, chromate and dichromate.
- a tension coating obtained by applying and baking a treatment liquid is proposed.
- Patent Document 7 discloses colloidal silica and phosphoric acid as tension coatings for grain-oriented electrical steel sheets mainly composed of colloidal silica and phosphate and not containing chromic anhydride, chromate or dichromate.
- An insulating coating treatment solution containing one or more selected from aluminum, boric acid, and sulfates of Mg, Al, Fe, Co, Ni, and Zn is disclosed.
- Patent Document 8 discloses a method for forming an insulating film that does not contain chromium oxide containing one or more selected from colloidal silica, magnesium phosphate, and sulfates of Mg, Al, Mn, and Zn. It is disclosed.
- Japanese Patent Publication No.57-2252 Japanese Examined Patent Publication No. 62-53579 Japanese Patent Publication No. 3-69968 Japanese Patent No. 3655123 JP 48-39338 A Japanese Patent Laid-Open No. 50-79442 Japanese Patent Publication No.57-9631 Japanese Examined Patent Publication No. 58-44744
- the grain-oriented electrical steel sheet that is the final product is cut into a length and a shape determined by a shear. And the cut
- a roll called a measuring roll is disposed on the front surface of the shear so as to come into contact with the steel sheet, and it is essential to determine the cutting position of the shear while measuring the steel sheet by rotating the roll.
- the present invention has been developed in view of the above situation, and has excellent noise characteristics in which noise can be kept low when a material having grooves for magnetic domain subdivision is assembled in an actual transformer.
- An object of the present invention is to provide an electrical steel sheet.
- the gist configuration of the present invention is as follows.
- the adhesion amount of the tension coating on the surface having the groove is A (g / m 2 )
- the adhesion amount of the tension coating on the surface without the groove is B (g / m 2 )
- the excellent noise characteristics in the steel sheet subjected to the magnetic domain subdivision treatment by the grooves are not impaired in the manufacturing process of the actual transformer, and therefore the excellent noise characteristics are also expressed in the actual transformer. Noise in the transformer can be kept low.
- the tension coating is applied to the surface of the steel sheet in which the groove is provided. It is characterized in that it defines the relationship between the amount of adhesion and the amount of adhesion of the tension coating on the surface without grooves.
- Patent Document 4 proposes a method of applying coating twice to improve the brittleness of the coating, but there is a problem that the manufacturing cost increases.
- the adhesion amount A (g / m 2 ) per unit area of the tension coating on the surface having the groove. 3 ⁇ A ⁇ 8 (1) That is, when the adhesion amount A is less than 3 g / m 2 , the tension application effect by the tension coating is small, and the noise is deteriorated. On the other hand, when the adhesion amount A exceeds 8 g / m 2 , the coating becomes brittle and the coating is peeled off at the corners of the groove under the pressure of the measuring roll to generate powder, which is pressed against the steel plate by the measuring roll. As a result, noise is degraded.
- noise can be improved by making B / A more than 1.0. This is because the tensile stress on the ground iron is increased and the sensitivity of the measuring roll to plastic strain is reduced compared to the case where the amount of adhesion on both sides where B / A is 1.0 is the same. It is thought that it was demonstrated effectively without being offset by the noise increase caused by However, if B / A exceeds 1.8, the noise will be deteriorated. This is considered to be due to the fact that the difference in tension between the tension coating and the tension coating was too large, and the steel sheet became convex.
- the component composition of the slab for grain-oriented electrical steel sheet may be a component composition that causes secondary recrystallization.
- the average deviation angle is preferably 5 ° or less.
- an inhibitor for example, when using an AlN-based inhibitor, Al and N, and when using an MnS / MnSe-based inhibitor, an appropriate amount of Mn and Se and / or S should be contained. Good. Of course, both inhibitors may be used in combination.
- the preferred contents of Al, N, S and Se are Al: 0.01 to 0.065 mass%, N: 0.005 to 0.012 mass%, S: 0.005 to 0.03 mass%, and Se: 0.005 to 0.03 mass%, respectively. .
- the present invention can also be applied to grain-oriented electrical steel sheets in which the contents of Al, N, S, and Se are limited and no inhibitor is used.
- the amounts of Al, N, S and Se are preferably suppressed to Al: 100 mass ppm or less, N: 50 mass ppm or less, S: 50 mass ppm or less, and Se: 50 mass ppm or less.
- the basic components and optional components of the slab for grain-oriented electrical steel sheets according to the present invention are specifically described as follows.
- C 0.15 mass% or less
- the lower limit since a secondary recrystallization is possible even for a material not containing C, it is not particularly necessary to provide it.
- Si 2.0-8.0% by mass Si is an element effective for increasing the electrical resistance of steel and improving iron loss, and its content of 2.0% by mass or more is particularly effective for reducing iron loss. On the other hand, when it is 8.0% by mass or less, particularly excellent workability and magnetic flux density can be obtained. Accordingly, the Si content is preferably in the range of 2.0 to 8.0% by mass.
- Mn 0.005 to 1.0 mass%
- Mn is an element advantageous for improving the hot workability, but if the content is less than 0.005% by mass, the effect of addition is poor. On the other hand, if it is 1.0 mass% or less, the magnetic flux density of a product board will become especially favorable. Therefore, the Mn content is preferably in the range of 0.005 to 1.0% by mass.
- Ni 0.03-1.50 mass%
- Sn 0.01-1.50 mass%
- Sb 0.005-1.50 mass%
- Cu 0.03-3.0 mass%
- P 0.03-0.50 mass%
- Mo 0.005-0.10 mass%
- Cr At least one Ni selected from 0.03 to 1.50 mass% is an element useful for further improving the hot rolled sheet structure and further improving the magnetic properties.
- the content is less than 0.03% by mass, the effect of improving the magnetic properties is small.
- the content is 1.5% by mass or less, the stability of secondary recrystallization is increased, and the magnetic properties are further improved. Therefore, the Ni content is preferably in the range of 0.03 to 1.5% by mass.
- Sn, Sb, Cu, P, Mo and Cr are elements useful for improving the magnetic properties, respectively, but if any of them is less than the lower limit of each component described above, the effect of improving the magnetic properties is small, When the amount is not more than the upper limit amount of each component described above, the development of secondary recrystallized grains is the best. For this reason, it is preferable to make it contain in said range, respectively.
- the balance other than the above components is inevitable impurities and Fe mixed in the manufacturing process.
- the slab having the above-described component composition is heated and subjected to hot rolling according to a conventional method, but may be immediately hot rolled after casting without being heated.
- hot rolling may be performed, or the hot rolling may be omitted and the process may proceed as it is.
- hot-rolled sheet annealing is performed as necessary.
- the main purpose of hot-rolled sheet annealing is to eliminate the band structure generated by hot rolling and to make the primary recrystallized structure sized, thereby further developing the goth structure and improving the magnetic properties in the secondary recrystallization annealing. That is.
- the hot-rolled sheet annealing temperature is preferably in the range of 800 to 1200 ° C.
- the hot-rolled sheet annealing temperature is less than 800 ° C, the band structure in hot rolling remains, making it difficult to achieve a sized primary recrystallized structure and obtaining the desired secondary recrystallization improvement. I can't.
- the hot-rolled sheet annealing temperature exceeds 1200 ° C.
- the grain size after the hot-rolled sheet annealing is excessively coarsened, so that it is very difficult to realize a sized primary recrystallized structure.
- decarburization annealing (also used for recrystallization annealing) is performed, and an annealing separator is applied.
- the steel sheet may be nitrided for the purpose of strengthening the inhibitor during the primary recrystallization annealing, or after the primary recrystallization annealing and before the start of the secondary recrystallization.
- a final finish annealing is performed for the purpose of forming a secondary recrystallization and a forsterite film (a film mainly composed of Mg 2 SiO 4 ).
- the annealing separator preferably contains MgO as a main component in order to form forsterite.
- MgO as a main component means that it may contain a known annealing separator component and property improving component other than MgO as long as it does not inhibit the formation of the forsterite film that is the object of the present invention. means.
- the groove formation according to the present invention may be performed in any step as long as it is after the final cold rolling, before and after primary recrystallization annealing, before and after secondary recrystallization annealing, and flattening annealing. Any process such as before and after is suitable. However, after tension coating, after removing the film at the groove forming position, a process of forming the groove by the method described later and forming the film again is necessary. Therefore, the groove formation is preferably performed after the final cold rolling and before the tension coating is formed.
- a tension coating is applied to the steel plate surface before or after the flattening annealing. It is also possible to apply a tension coating treatment solution before the flattening annealing to serve as both flattening annealing and coating baking.
- this tension coating means a coating capable of imparting tension to a steel sheet in order to reduce iron loss in the present invention.
- any one having silica and phosphate as main components is advantageously suitable.
- the main component is 5 to 30% by mass of colloidal silica and 5 to 30% by mass of primary phosphates of Mg, Ca, Ba, Sr, Zn, Al and Mn.
- a known additive such as chromic anhydride, Mg, Al, Mn and Zn sulfate, Fe, Ni hydroxide, and the like is applied to the steel sheet, and the temperature is 350 ° C. or higher and 1000 ° C. or lower.
- a suitable tension coating is obtained by baking at a temperature of 700 ° C. or higher and 900 ° C. or lower.
- channel is formed in the surface of a grain-oriented electrical steel sheet in any process before and after primary recrystallization annealing, before and after secondary recrystallization annealing, and before and after flattening annealing after the last cold rolling.
- the groove formation in the present invention includes a conventionally known groove formation method, for example, a local etching method, a scribing method with a blade, a rolling method using a roll with protrusions, etc., and the most preferable method.
- an etching resist is attached to the steel sheet after the final cold rolling by printing or the like, and then a groove is formed in the non-attached region by a process such as electrolytic etching.
- the groove formed on the surface of the steel sheet according to the present invention has a width of 50 to 300 ⁇ m, a depth of 10 to 50 ⁇ m and a spacing of about 1.5 to 20.0 mm, and the direction perpendicular to the rolling direction of the linear groove The deviation is preferably within ⁇ 30 °.
- “linear” includes not only a solid line but also a dotted line and a broken line.
- a conventionally known method for manufacturing a grain-oriented electrical steel sheet in which grooves are formed and magnetic domain subdivision processing is performed may be applied.
- a steel slab having a composition as described above was manufactured by continuous casting, heated to 1400 ° C., hot rolled into a hot rolled sheet having a thickness of 2.2 mm, and then subjected to hot rolled sheet annealing at 1000 ° C. Subsequently, the intermediate plate thickness was set to 1.0 mm by cold rolling, and intermediate annealing was performed at 1000 ° C. Thereafter, cold rolling was performed to obtain a cold-rolled sheet having a thickness of 0.23 mm.
- an etching resist is applied by gravure offset printing, and then a linear groove having a width of 150 ⁇ m and a depth of 20 ⁇ m is formed by 10 ° with respect to the direction perpendicular to the rolling direction by electrolytic etching and resist stripping in an alkaline solution. They were formed at intervals of 3 mm in the rolling direction at an inclination angle.
- decarburization annealing was performed at 825 ° C
- an annealing separator mainly composed of MgO was applied, and final finishing annealing for the purpose of secondary recrystallization and purification was performed at 1200 ° C and 10 hours. .
- the tension coating processing liquid which consists of 20 mass% colloidal silica and 10 mass% primary magnesium phosphate was apply
- the resulting product was evaluated for magnetic properties and film tension.
- the tension coating adhesion amount A (g / m 2 ) on the surface having the groove and the tension coating adhesion amount B (g / m 2 ) on the surface without the groove were changed as shown in Table 1.
- the adhesion amount A (g / m 2 ) and the adhesion amount B (g / m 2 ) were measured by the weight difference between the steel sheets before and after the coating removal.
- the steel plate is sheared to 100 mm x 100 mm, 10 sheets, the non-measurement surface is covered with tape, the steel plate is immersed in a high-temperature and high-concentration NaOH aqueous solution, the coating on the measurement surface is removed, and coating is performed. It calculated
- the steel sheet was measured with a measuring roll (pressing force: 350 N) with a diameter of 50 mm and a width of 50 mm.
- a transformer was fabricated and the noise was measured when excited at 50Hz and 1.7T. The above noise measurement results are also shown in Table 1.
- a steel slab having a composition as described above was manufactured by continuous casting, heated to 1400 ° C., hot rolled into a hot rolled sheet having a thickness of 2.2 mm, and then subjected to hot rolled sheet annealing at 1000 ° C. Subsequently, the intermediate plate thickness was set to 1.0 mm by cold rolling, and intermediate annealing was performed at 1000 ° C. Thereafter, cold rolling was performed to obtain a cold-rolled sheet having a thickness of 0.23 mm.
- the film is removed in a line in a direction perpendicular to the rolling direction by irradiating a laser, and then a linear groove having a width of 150 ⁇ m and a depth of 20 ⁇ m is formed by electrolytic etching. They were formed at intervals of 3 mm in the rolling direction at an inclination angle of 10 ° with respect to the direction perpendicular to the rolling direction. Thereafter, a tension coating composed of 50% colloidal silica and magnesium phosphate was applied again to obtain a product.
- the tension coating adhesion amount A (g / m 2 ) on the surface having the groove and the tension coating adhesion amount B (g / m 2 ) on the surface without the groove were changed as shown in Table 2.
- the adhesion amount of each tension coating is the total amount of the first coating and the second coating, and was measured in the same manner as in Example 1.
- the steel sheet was measured with a measuring roll (pressing force: 500 N) with a diameter of 60 mm and a width of 100 mm.
- a transformer was fabricated and the noise was measured when excited at 50Hz and 1.7T. The above noise measurement results are also shown in Table 2.
- a steel slab was manufactured by continuous casting, heated to 1400 ° C., hot rolled into a hot rolled sheet with a thickness of 2.2 mm, and then annealed at 1000 ° C. Subsequently, the intermediate sheet thickness was set to 2.0 mm by cold rolling, and after intermediate annealing at 1000 ° C., cold rolling was performed to obtain a cold rolled sheet having a sheet thickness of 0.29 mm.
- an etching resist is applied by gravure offset printing, and then a linear groove having a width of 150 ⁇ m and a depth of 20 ⁇ m is formed by 10 ° with respect to the direction perpendicular to the rolling direction by electrolytic etching and resist stripping in an alkaline solution. They were formed at intervals of 3 mm in the rolling direction at an inclination angle.
- decarburization annealing was performed at 825 ° C
- an annealing separator mainly composed of MgO was applied, and final finishing annealing for the purpose of secondary recrystallization and purification was performed at 1200 ° C and 10 hours. .
- the steel plate is sheared to 100 mm x 100 mm, 10 sheets, the non-measurement surface is covered with tape, the steel plate is immersed in a high-temperature and high-concentration NaOH aqueous solution, the coating on the measurement surface is removed, and coating is performed. It calculated
- the steel sheet was measured with a measuring roll (pressing force: 350 N) with a diameter of 50 mm and a width of 50 mm.
- a transformer was fabricated and the noise was measured when excited at 50Hz and 1.7T. The above noise measurement results are also shown in Table 3.
Abstract
Description
そのためには、鋼板中の二次再結晶粒を、(110)[001]方位(いわゆる、ゴス方位)に高度に揃えることや、製品鋼板中の不純物を低減することが重要である。しかしながら、結晶方位の制御や、不純物を低減することは、製造コストとの兼ね合い等で限界がある。そこで、鋼板の表面に対して物理的あるいは化学的な手法で不均一歪や溝を導入し、磁区の幅を細分化して鉄損を低減する技術、すなわち磁区細分化技術が開発されている。 The grain-oriented electrical steel sheet is mainly used as an iron core of a transformer and is required to have excellent magnetization characteristics, particularly low iron loss.
For this purpose, it is important to highly align the secondary recrystallized grains in the steel sheet in the (110) [001] orientation (so-called Goth orientation) and to reduce impurities in the product steel sheet. However, control of crystal orientation and reduction of impurities are limited in view of the manufacturing cost. In view of this, a technique for reducing the iron loss by introducing non-uniform strains or grooves into the surface of the steel sheet by physical or chemical techniques and subdividing the width of the magnetic domain, that is, a magnetic domain refinement technique has been developed.
また、特許文献2には、仕上げ焼鈍済みの鋼板に対して、882~2156 MPa(90~220 kgf/mm2)の荷重で地鉄部分に深さ:5μm 超の溝を形成したのち、750℃以上の温度で加熱処理することにより、磁区を細分化する技術が提案されている。
特許文献3には、鋼板の圧延方向とほぼ直角な方向に幅30μm以上300μm以下、深さ10μm以上70μm以下、圧延方向の間隔1mm以上の線状刻み目(溝)を導入する技術が提案されている。
上記のような磁区細分化技術の開発により、鉄損特性が良好な方向性電磁鋼板が得られるようになってきている。 For example, Patent Document 1 proposes a technique for reducing the iron loss of a steel sheet by irradiating a final product plate with a laser, introducing a high dislocation density region into the steel sheet surface layer, and narrowing the magnetic domain width.
In Patent Document 2, a steel sheet that has been subjected to finish annealing is formed with a groove having a depth of more than 5 μm in the base iron portion under a load of 882 to 2156 MPa (90 to 220 kgf / mm 2 ), and then 750 There has been proposed a technique for subdividing magnetic domains by heat treatment at a temperature equal to or higher than ° C.
Patent Document 3 proposes a technique for introducing linear notches (grooves) having a width of 30 μm or more and 300 μm or less, a depth of 10 μm or more and 70 μm or less, and an interval of 1 mm or more in the rolling direction in a direction substantially perpendicular to the rolling direction of the steel sheet. Yes.
With the development of the magnetic domain fragmentation technology as described above, grain oriented electrical steel sheets having good iron loss characteristics have been obtained.
発明者らが発見したところでは、上述した溝形成により磁区細分化処理を施す技術では、図1に示すように、メジャーリングロールRによる押圧時に、圧下応力が集中する溝1の縁(角)の部分10で塑性歪が発生しやすく、これが変圧器騒音を増加する原因になることが明らかとなった。 By the way, the grain-oriented electrical steel sheet that is the final product is cut into a length and a shape determined by a shear. And the cut | disconnected electromagnetic steel plate is laminated | stacked and becomes an iron core of a transformer. When cutting with this shear, the cutting length is required to have very high accuracy. Therefore, a roll called a measuring roll is disposed on the front surface of the shear so as to come into contact with the steel sheet, and it is essential to determine the cutting position of the shear while measuring the steel sheet by rotating the roll.
As discovered by the inventors, in the technique for performing magnetic domain subdivision processing by the groove formation described above, the edge (corner) of the groove 1 where the rolling stress is concentrated when pressed by the measuring roll R as shown in FIG. It has been clarified that plastic strain is likely to occur in the
鋼板表裏面のいずれか片面に磁区細分化を司る溝を有し、該鋼板の表裏面にフォルステライト被膜および張力コーティングをそなえる方向性電磁鋼板であって、
前記溝を有する面における張力コーティングの付着量をA(g/m2)および、前記溝のない面における張力コーティングの付着量をB(g/m2)とするとき、これらの付着量AおよびBが下記式(1)および(2)を満足する方向性電磁鋼板。
記
3≦A≦8 …(1)
1.0<B/A≦1.8 …(2) That is, the gist configuration of the present invention is as follows.
A grain-oriented electrical steel sheet having grooves for controlling magnetic domain subdivision on either side of the steel sheet front and back surfaces, and having a forsterite film and a tension coating on the front and back surfaces of the steel sheet,
When the adhesion amount of the tension coating on the surface having the groove is A (g / m 2 ) and the adhesion amount of the tension coating on the surface without the groove is B (g / m 2 ), these adhesion amounts A and A grain-oriented electrical steel sheet in which B satisfies the following formulas (1) and (2).
3 ≦ A ≦ 8 (1)
1.0 <B / A ≦ 1.8 (2)
本発明では、磁区細分化用の溝形成を行った方向性電磁鋼板を実機トランスに供した際の、該トランスにおける騒音特性の劣化を防止するために、鋼板の溝を設けた面に対する張力コーティングの付着量および溝のない面の張力コーティングの付着量の関係について規定するところに特徴がある。かような規定によって、溝のない面の張力コーティングの膜厚を、溝のある面の張力コーティングの膜厚より厚くすることにより、メジャーリングロールの圧下に伴う塑性歪に起因する、変圧器騒音の増加を抑制することができる。 Hereinafter, the present invention will be specifically described.
In the present invention, in order to prevent deterioration of noise characteristics in the transformer when the grain-oriented electrical steel sheet in which the grooves for magnetic domain subdivision have been formed is used in an actual transformer, the tension coating is applied to the surface of the steel sheet in which the groove is provided. It is characterized in that it defines the relationship between the amount of adhesion and the amount of adhesion of the tension coating on the surface without grooves. By making the film thickness of the tension coating on the non-grooved surface thicker than the film thickness of the tension coating on the grooved surface, the transformer noise caused by plastic strain accompanying the reduction of the measuring roll Can be suppressed.
3≦A≦8 …(1)
すなわち、付着量Aが3g/m2未満では、張力コーティングによる張力付与効果が小さく、騒音が劣化してしまう。一方、付着量Aが8g/m2超では、コーティングが脆化し、メジャーリングロールでの圧下で溝の角部分でコーティングが剥がれて、粉が発生し、それがメジャーリングロールで鋼板に押し付けられて歪を生じるため、やはり騒音が劣化してしまう。 Therefore, in the present invention, first, it is necessary to satisfy the following expression (1) for the adhesion amount A (g / m 2 ) per unit area of the tension coating on the surface having the groove.
3 ≦ A ≦ 8 (1)
That is, when the adhesion amount A is less than 3 g / m 2 , the tension application effect by the tension coating is small, and the noise is deteriorated. On the other hand, when the adhesion amount A exceeds 8 g / m 2 , the coating becomes brittle and the coating is peeled off at the corners of the groove under the pressure of the measuring roll to generate powder, which is pressed against the steel plate by the measuring roll. As a result, noise is degraded.
1.0<B/A≦1.8 …(2)
の範囲に規制することが肝要である。
ここに、溝のない面は鋼板表面の凹凸がないため、張力コーティングの付着量が増えても、張力コーティングが粉化することはない。したがって、粉体が鋼板面に押し込まれることに起因した騒音が生じるという弊害も生じない。一方、溝を有する面では、やはり溝の角(縁)部分がメジャーリングロールに圧下されれば塑性歪が生じるが、反対側の溝のない面で張力コーティングの厚みを増加させれば、前記した粉体の弊害なく、前記の塑性歪に起因した騒音を低減することができる。 Further, when the adhesion amount per unit area of the tension coating with no groove surface was B (g / m 2), 1.0 the ratio B / A of the above-mentioned coating weight A (g / m 2) < B / A ≦ 1.8 (2)
It is important to regulate to this range.
Here, since the surface without the groove has no irregularities on the surface of the steel sheet, the tension coating is not pulverized even if the adhesion amount of the tension coating increases. Accordingly, there is no adverse effect that noise is generated due to the powder being pushed into the steel plate surface. On the other hand, on the surface having the groove, plastic distortion occurs if the corner (edge) portion of the groove is pressed down to the measuring roll, but if the thickness of the tension coating is increased on the surface without the groove on the opposite side, The noise caused by the plastic strain can be reduced without the harmful effects of the powder.
本発明において、方向性電磁鋼板用スラブの成分組成は、二次再結晶が生じる成分組成であればよい。なお、圧延方向に対する、製品結晶粒の<100>方位のずれ角が小さいほど、磁区細分化による鉄損低減効果は大きくなるため、その平均のずれ角は、5°以下であることが好ましい。
また、インヒビターを利用する場合、例えばAlN系インヒビターを利用する場合であればAlおよびNを、またMnS・MnSe系インヒビターを利用する場合であればMnとSeおよび/またはSを適量含有させればよい。勿論、両インヒビターを併用してもよい。この場合におけるAl、N、SおよびSeの好適含有量はそれぞれ、Al:0.01~0.065質量%、N:0.005~0.012質量%、S:0.005~0.03質量%、Se:0.005~0.03質量%である。 Next, the manufacturing conditions of the grain-oriented electrical steel sheet according to the present invention will be specifically described.
In the present invention, the component composition of the slab for grain-oriented electrical steel sheet may be a component composition that causes secondary recrystallization. Note that the smaller the deviation angle of the <100> orientation of the product crystal grains with respect to the rolling direction, the greater the effect of reducing iron loss due to magnetic domain fragmentation. Therefore, the average deviation angle is preferably 5 ° or less.
Further, when using an inhibitor, for example, when using an AlN-based inhibitor, Al and N, and when using an MnS / MnSe-based inhibitor, an appropriate amount of Mn and Se and / or S should be contained. Good. Of course, both inhibitors may be used in combination. In this case, the preferred contents of Al, N, S and Se are Al: 0.01 to 0.065 mass%, N: 0.005 to 0.012 mass%, S: 0.005 to 0.03 mass%, and Se: 0.005 to 0.03 mass%, respectively. .
この場合には、Al、N、SおよびSe量はそれぞれ、Al:100 質量ppm以下、N:50 質量ppm以下、S:50 質量ppm以下、Se:50 質量ppm以下に抑制することが好ましい。 Furthermore, the present invention can also be applied to grain-oriented electrical steel sheets in which the contents of Al, N, S, and Se are limited and no inhibitor is used.
In this case, the amounts of Al, N, S and Se are preferably suppressed to Al: 100 mass ppm or less, N: 50 mass ppm or less, S: 50 mass ppm or less, and Se: 50 mass ppm or less.
C:0.15質量%以下
Cは、熱延板組織の改善のために添加をするが、0.15質量%を超えると製造工程中に磁気時効の起こらない50質量ppm以下までCを低減する負担が増大するため、0.15質量%以下とすることが好ましい。なお、下限に関しては、Cを含まない素材でも二次再結晶が可能であるので特に設ける必要はない。 The basic components and optional components of the slab for grain-oriented electrical steel sheets according to the present invention are specifically described as follows.
C: 0.15 mass% or less C is added to improve the hot-rolled sheet structure, but if it exceeds 0.15 mass%, the burden of reducing C to 50 mass ppm or less at which no magnetic aging occurs during the manufacturing process increases. Therefore, the content is preferably 0.15% by mass or less. In addition, regarding the lower limit, since a secondary recrystallization is possible even for a material not containing C, it is not particularly necessary to provide it.
Siは、鋼の電気抵抗を高め、鉄損を改善するのに有効な元素であり、含有量が2.0質量%以上でとくに鉄損低減効果が良好である。一方、8.0質量%以下の場合、とくに優れた加工性や磁束密度を得ることができる。従って、Si量は2.0~8.0質量%の範囲とすることが好ましい。 Si: 2.0-8.0% by mass
Si is an element effective for increasing the electrical resistance of steel and improving iron loss, and its content of 2.0% by mass or more is particularly effective for reducing iron loss. On the other hand, when it is 8.0% by mass or less, particularly excellent workability and magnetic flux density can be obtained. Accordingly, the Si content is preferably in the range of 2.0 to 8.0% by mass.
Mnは、熱間加工性を良好にする上で有利な元素であるが、含有量が0.005質量%未満ではその添加効果に乏しい。一方1.0質量%以下とすると製品板の磁束密度がとくに良好となる。このため、Mn量は0.005~1.0質量%の範囲とすることが好ましい。 Mn: 0.005 to 1.0 mass%
Mn is an element advantageous for improving the hot workability, but if the content is less than 0.005% by mass, the effect of addition is poor. On the other hand, if it is 1.0 mass% or less, the magnetic flux density of a product board will become especially favorable. Therefore, the Mn content is preferably in the range of 0.005 to 1.0% by mass.
Ni:0.03~1.50質量%、Sn:0.01~1.50質量%、Sb:0.005~1.50質量%、Cu:0.03~3.0質量%、P:0.03~0.50質量%、Mo:0.005~0.10質量%およびCr:0.03~1.50質量%のうちから選んだ少なくとも1種
Niは、熱延板組織をさらに改善して磁気特性を一層向上させるために有用な元素である。しかしながら、含有量が0.03質量%未満では磁気特性の向上効果が小さく、一方1.5質量%以下ではとくに二次再結晶の安定性が増し、磁気特性がさらに改善される。そのため、Ni量は0.03~1.5質量%の範囲とするのが好ましい。 In addition to the above basic components, the following elements can be appropriately contained as magnetic property improving components.
Ni: 0.03-1.50 mass%, Sn: 0.01-1.50 mass%, Sb: 0.005-1.50 mass%, Cu: 0.03-3.0 mass%, P: 0.03-0.50 mass%, Mo: 0.005-0.10 mass%, and Cr: At least one Ni selected from 0.03 to 1.50 mass% is an element useful for further improving the hot rolled sheet structure and further improving the magnetic properties. However, if the content is less than 0.03% by mass, the effect of improving the magnetic properties is small. On the other hand, if the content is 1.5% by mass or less, the stability of secondary recrystallization is increased, and the magnetic properties are further improved. Therefore, the Ni content is preferably in the range of 0.03 to 1.5% by mass.
なお、上記成分以外の残部は、製造工程において混入する不可避的不純物およびFeである。 Sn, Sb, Cu, P, Mo and Cr are elements useful for improving the magnetic properties, respectively, but if any of them is less than the lower limit of each component described above, the effect of improving the magnetic properties is small, When the amount is not more than the upper limit amount of each component described above, the development of secondary recrystallized grains is the best. For this reason, it is preferable to make it contain in said range, respectively.
The balance other than the above components is inevitable impurities and Fe mixed in the manufacturing process.
焼鈍分離剤は、フォルステライトを形成するためMgOを主成分とするものが好適である。ここで、MgOが主成分であるとは、本発明の目的とするフォルステライト被膜の形成を阻害しない範囲で、MgO以外の公知の焼鈍分離剤成分や特性改善成分を含有してもよいことを意味する。
なお、以下に説明するように、本発明に従う溝の形成は、最終の冷間圧延の後であれば、いずれの工程でもよく、一次再結晶焼鈍前後、二次再結晶焼鈍前後、平坦化焼鈍前後など、いずれの工程も適合する。但し、張力コーティング後は、溝形成位置の被膜を取り除いてから、後述する手法にて溝を形成し、再び被膜を形成する工程が必要になる。したがって、溝形成は、最終冷間圧延後であって、張力コーティング被成前に行うことが好ましい。 After hot-rolled sheet annealing, after one cold rolling or two or more cold rollings sandwiching intermediate annealing, decarburization annealing (also used for recrystallization annealing) is performed, and an annealing separator is applied. . The steel sheet may be nitrided for the purpose of strengthening the inhibitor during the primary recrystallization annealing, or after the primary recrystallization annealing and before the start of the secondary recrystallization. After the annealing separator is applied before the secondary recrystallization annealing, a final finish annealing is performed for the purpose of forming a secondary recrystallization and a forsterite film (a film mainly composed of Mg 2 SiO 4 ).
The annealing separator preferably contains MgO as a main component in order to form forsterite. Here, MgO as a main component means that it may contain a known annealing separator component and property improving component other than MgO as long as it does not inhibit the formation of the forsterite film that is the object of the present invention. means.
As will be described below, the groove formation according to the present invention may be performed in any step as long as it is after the final cold rolling, before and after primary recrystallization annealing, before and after secondary recrystallization annealing, and flattening annealing. Any process such as before and after is suitable. However, after tension coating, after removing the film at the groove forming position, a process of forming the groove by the method described later and forming the film again is necessary. Therefore, the groove formation is preferably performed after the final cold rolling and before the tension coating is formed.
ここに、この張力コーティングは、本発明では、鉄損低減のために、鋼板に張力を付与できるコーティングを意味する。なお、張力コーティングとしては、シリカおよびリン酸塩を主成分とするもののいずれもが有利に適合する。
具体的には、例えばコロイダルシリカ5~30質量%、および、Mg、Ca、Ba、Sr、Zn、AlおよびMnの第一りん酸塩5~30質量%を主成分とし、必要に応じて、公知の添加物、たとえば無水クロム酸、Mg、Al、MnおよびZnの硫酸塩、Fe、Niの水酸化物などを添加したコーティング処理液を鋼板に塗布し、350℃以上1000℃以下の温度、好ましくは、700℃以上900℃以下の温度で焼き付けることによって、好適な張力コーティングが得られる。 After the final finish annealing, it is effective to correct the shape by performing flattening annealing. In the present invention, a tension coating is applied to the steel plate surface before or after the flattening annealing. It is also possible to apply a tension coating treatment solution before the flattening annealing to serve as both flattening annealing and coating baking. In the present invention, when tension coating is applied to a steel sheet, it is important to control the coating adhesion amounts on the surface having grooves and on the surface without grooves.
Here, this tension coating means a coating capable of imparting tension to a steel sheet in order to reduce iron loss in the present invention. As the tension coating, any one having silica and phosphate as main components is advantageously suitable.
Specifically, for example, the main component is 5 to 30% by mass of colloidal silica and 5 to 30% by mass of primary phosphates of Mg, Ca, Ba, Sr, Zn, Al and Mn. A known additive, such as chromic anhydride, Mg, Al, Mn and Zn sulfate, Fe, Ni hydroxide, and the like is applied to the steel sheet, and the temperature is 350 ° C. or higher and 1000 ° C. or lower. Preferably, a suitable tension coating is obtained by baking at a temperature of 700 ° C. or higher and 900 ° C. or lower.
本発明での溝の形成は、従来公知の溝の形成方法、例えば、局所的にエッチング処理する方法、刃物などでけがく方法、突起つきロールで圧延する方法などが挙げられるが、最も好ましい方法は、最終冷延後の鋼板に印刷等によりエッチングレジストを付着させたのち、非付着域に電解エッチング等の処理により溝を形成する方法である。 Moreover, in this invention, a groove | channel is formed in the surface of a grain-oriented electrical steel sheet in any process before and after primary recrystallization annealing, before and after secondary recrystallization annealing, and before and after flattening annealing after the last cold rolling.
The groove formation in the present invention includes a conventionally known groove formation method, for example, a local etching method, a scribing method with a blade, a rolling method using a roll with protrusions, etc., and the most preferable method. In this method, an etching resist is attached to the steel sheet after the final cold rolling by printing or the like, and then a groove is formed in the non-attached region by a process such as electrolytic etching.
次に、825℃で脱炭焼鈍を施したのち、MgOを主成分とする焼鈍分離剤を塗布し、二次再結晶と純化を目的とした最終仕上げ焼鈍を1200℃および10hの条件で実施した。
そして、20質量%のコロイダルシリカと10質量%の第一リン酸マグネシウムからなる張力コーティング処理液を塗布し、830℃で、張力コーティング焼付けを兼ねた平坦化焼鈍を行って製品とした。得られた製品について、磁気特性および被膜張力を評価した。その際、溝を有する面の張力コーティング付着量A(g/m2)と溝のない面の張力コーティング付着量B(g/m2)とを、表1に示すように変化させた。なお、付着量A(g/m2)および付着量B(g/m2)は、コーティング除去前後の鋼板の重量差にて測定した。具体的には、鋼板を100mm×100mm、10枚にせん断し、非測定面をテープで覆った後、高温かつ高濃度のNaOH水溶液中に鋼板を浸漬し、測定面のコーティングを除去し、コーティング除去前後の鋼板の重量差より、1m2当たりの付着量に換算して求めた。その測定結果を表1に示す。 After that, an etching resist is applied by gravure offset printing, and then a linear groove having a width of 150 μm and a depth of 20 μm is formed by 10 ° with respect to the direction perpendicular to the rolling direction by electrolytic etching and resist stripping in an alkaline solution. They were formed at intervals of 3 mm in the rolling direction at an inclination angle.
Next, after decarburization annealing was performed at 825 ° C, an annealing separator mainly composed of MgO was applied, and final finishing annealing for the purpose of secondary recrystallization and purification was performed at 1200 ° C and 10 hours. .
And the tension coating processing liquid which consists of 20 mass% colloidal silica and 10 mass% primary magnesium phosphate was apply | coated, and the flattening annealing which served as tension coating baking was performed at 830 degreeC, and it was set as the product. The resulting product was evaluated for magnetic properties and film tension. At that time, the tension coating adhesion amount A (g / m 2 ) on the surface having the groove and the tension coating adhesion amount B (g / m 2 ) on the surface without the groove were changed as shown in Table 1. The adhesion amount A (g / m 2 ) and the adhesion amount B (g / m 2 ) were measured by the weight difference between the steel sheets before and after the coating removal. Specifically, the steel plate is sheared to 100 mm x 100 mm, 10 sheets, the non-measurement surface is covered with tape, the steel plate is immersed in a high-temperature and high-concentration NaOH aqueous solution, the coating on the measurement surface is removed, and coating is performed. It calculated | required in conversion to the adhesion amount per 1 m < 2 > from the weight difference of the steel plate before and behind removal. The measurement results are shown in Table 1.
上記した騒音測定結果を表1に併記する。 Next, for each product, the steel sheet was measured with a measuring roll (pressing force: 350 N) with a diameter of 50 mm and a width of 50 mm. A transformer was fabricated and the noise was measured when excited at 50Hz and 1.7T.
The above noise measurement results are also shown in Table 1.
上記した騒音測定結果を表2に併記する。 Next, for each product, the steel sheet was measured with a measuring roll (pressing force: 500 N) with a diameter of 60 mm and a width of 100 mm. A transformer was fabricated and the noise was measured when excited at 50Hz and 1.7T.
The above noise measurement results are also shown in Table 2.
次に、825℃で脱炭焼鈍を施したのち、MgOを主成分とする焼鈍分離剤を塗布し、二次再結晶と純化を目的とした最終仕上げ焼鈍を1200℃および10hの条件で実施した。
そして、表3に示す種々の張力コーティング処理液を塗布し、830℃で、張力コーティング焼付けを兼ねた平坦化焼鈍を行って製品とした。得られた製品について、磁気特性および被膜張力を評価した。その際、溝を有する面の張力コーティング付着量A(g/m2)と溝のない面の張力コーティング付着量B(g/m2)とを、表3に示すように変化させた。なお、付着量A(g/m2)および付着量B(g/m2)は、コーティング除去前後の鋼板の重量差にて測定した。具体的には、鋼板を100mm×100mm、10枚にせん断し、非測定面をテープで覆った後、高温かつ高濃度のNaOH水溶液中に鋼板を浸漬し、測定面のコーティングを除去し、コーティング除去前後の鋼板の重量差より、1m2当たりの付着量に換算して求めた。その測定結果を表3に示す。 After that, an etching resist is applied by gravure offset printing, and then a linear groove having a width of 150 μm and a depth of 20 μm is formed by 10 ° with respect to the direction perpendicular to the rolling direction by electrolytic etching and resist stripping in an alkaline solution. They were formed at intervals of 3 mm in the rolling direction at an inclination angle.
Next, after decarburization annealing was performed at 825 ° C, an annealing separator mainly composed of MgO was applied, and final finishing annealing for the purpose of secondary recrystallization and purification was performed at 1200 ° C and 10 hours. .
Then, various tension coating treatment solutions shown in Table 3 were applied, and flattening annealing was performed at 830 ° C., which also served as tension coating baking, to obtain products. The resulting product was evaluated for magnetic properties and film tension. At that time, the tension coating adhesion amount A (g / m 2 ) on the surface having the groove and the tension coating adhesion amount B (g / m 2 ) on the surface without the groove were changed as shown in Table 3. The adhesion amount A (g / m 2 ) and the adhesion amount B (g / m 2 ) were measured by the weight difference between the steel sheets before and after the coating removal. Specifically, the steel plate is sheared to 100 mm x 100 mm, 10 sheets, the non-measurement surface is covered with tape, the steel plate is immersed in a high-temperature and high-concentration NaOH aqueous solution, the coating on the measurement surface is removed, and coating is performed. It calculated | required in conversion to the adhesion amount per 1 m < 2 > from the weight difference of the steel plate before and behind removal. The measurement results are shown in Table 3.
上記した騒音測定結果を表3に併記する。 Next, for each product, the steel sheet was measured with a measuring roll (pressing force: 350 N) with a diameter of 50 mm and a width of 50 mm. A transformer was fabricated and the noise was measured when excited at 50Hz and 1.7T.
The above noise measurement results are also shown in Table 3.
10 角(縁)部分
R メジャーリングロール
1 Groove 10 Corner (edge) part R Majoring roll
Claims (1)
- 鋼板表裏面のいずれか片面に磁区細分化を司る溝を有し、該鋼板の表裏面にフォルステライト被膜および張力コーティングをそなえる方向性電磁鋼板であって、
前記溝を有する面における張力コーティングの付着量をA(g/m2)および、前記溝のない面における張力コーティングの付着量をB(g/m2)とするとき、これらの付着量AおよびBが下記式(1)および(2)を満足する方向性電磁鋼板。
記
3≦A≦8 …(1)
1.0<B/A≦1.8 …(2) A grain-oriented electrical steel sheet having grooves for controlling magnetic domain subdivision on either side of the steel sheet front and back surfaces, and having a forsterite film and a tension coating on the front and back surfaces of the steel sheet,
When the adhesion amount of the tension coating on the surface having the groove is A (g / m 2 ) and the adhesion amount of the tension coating on the surface without the groove is B (g / m 2 ), these adhesion amounts A and A grain-oriented electrical steel sheet in which B satisfies the following formulas (1) and (2).
3 ≦ A ≦ 8 (1)
1.0 <B / A ≦ 1.8 (2)
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KR102177038B1 (en) | 2014-11-14 | 2020-11-10 | 주식회사 포스코 | Insulation coating composite for oriented electrical steel steet, oriented electrical steel steet formed insulation coating film on using the same insulation coating composite, and method of manufacturing the same oriented electrical steel steet |
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